GB2170222A

GB2170222A - Wear-resistant alloy of high permeability and method of producing the same

Info

Publication number: GB2170222A
Application number: GB08519403A
Authority: GB
Inventors: Hakaru Masumoto; Yuetsu Murakami
Original assignee: ZAIDAN HOJIN DENKI JIKI ZAIRYO
Current assignee: ZAIDAN HOJIN DENKI JIKI ZAIRYO
Priority date: 1985-01-30
Filing date: 1985-08-01
Publication date: 1986-07-30
Also published as: US4834813A; KR860005901A; CN1048567A; CN1019672B; KR910002868B1; CN1052702A; GB8519403D0; JPH0545658B2; JPS61174349A; CN1011983B; US4830685A; US4710243A; CN85106170A; GB2170222B

Description

GB2170222A 1

SPECIFICATION

Wear-resistant alloy of high permeability and method of producing the same The present invention relates to a wear-resistant alloy of high permeability consisting essentially 5 of Ni, Nb and Fe, a wear-resistant alloy of high permeability comprising Ni, Nb and Fe as main components and at least one subsidiary component selected from the group consisting of Cr, Mo, Ge, Au, Co, V, W, Ta, Cu, Mn, Al, Si, Ti, Zr, Hf, Sn, Sb, Ga, In, TI, Zn, Cd, rare earth elementsl platinum group metals, Be, Ag, Sr, Ba, B, P and S, and methods of producing the same. 10 Heretofore, magnetic record play-back heads of tape-recorders and the like are operated in A.C. magnetic field, so that magnetic alloys used therefor are required to have high effective permeability in high frequency magnetic field and a good wear-resistant property because they contact with sliding magnetic tapes. Recently, as wear-resistant magnetic alloys for magnetic head there are Sendust which is an Fe-Si-AI series alloy and Mn-Zn ferrite which is an MnO- 15 ZnO-Fe,O, alloy. However, these alloys have drawbacks in that they are so hard and brittle that they can not be forged or rolled and have to exclusively be processed to head cores by - laborsome and time-consuming cutting or grinding work, so that the products are very expen sive. Though Sendust has a high magnetic flux density, it can not be processed to a thin plate, so that it has a shortcoming of a relatively low effective permeability value in a high frequency 20 magnetic field. While ferrite has a high effective permeability, it has a shortcoming of a low saturation magnetic flux density of about 4,000 G. On the other hand, Permalloy which is an Ni Fe series alloy has a high saturation magnetic-flux density, however, it has a drawback of a low effective permeability. Though Permalloy can be mass produced easily by forging, rolling or punching, it has also a reat drawback of low wear-resistance. 25 The inventors had previously found out that an Ni-Fe-Nb series alloy and an Ni-Fe-Ta series alloy are easy to be worked or processed by forging and have high hardness and permeability so that they are suited well to magnetic alloys for magnetic heads, and filed patent applications therefor which matured to U.S. patent Nos. 3,743,550 and 3,785,880.

Afterwards, the inventors have produced thin plates of the Ni-Fe-Nb series and Ni-Fe-Ta series 30 alloys for magnetic alloys for magnetic heads. As a result, the inventors have found out a great problem that abrasion or wear-resistant property of a magnetic head made of the thin plate caused by sliding contact of a magnetic tape thereon varies noticeably depending on manners of working and heat treatment in the process of producing the thin plate, and that the wear resistant property of the thin plate often shows a considerably inferior value depending on the 35 manners of working and heat treatment.

Therefore, an object of the present invention is to obviate or mitigate the aforementioned drawbacks, shortcomings and problems of the prior art.

Another object of the present invention is to provide a wear-resistant alloy of high permeabil ity distinguished over prior alloys. 40 These objects are achieved by the present invention.

In order to scrutinize the cause of the above-described problem of the NiFe-Nb series and Ni Fe-Ta series alloys, the inventors have made a series of systematic studies and researches about the wear or abrasion of these alloys. As a result, it was found out that the wear of these alloys is not primarily determined by their hardness and is closely related to a recrystallization texture 45 which depends on the manners of producing the thin plate of these alloys.

Though it is-generally known that abrasion phenomenon -of an alloy varies largely depending on orientation-of crystals of the alloy and that crystal anisotropic property exists in the alloy, the inventors have found out that in the Ni-Fe-Nb series and Ni-Fe-Ta series alloys the alloys are liable to wear at crystal orientation of 111 011<00 1 >, and that crystal orientations of 50 11 001< 1 12> and 1311 J< 1 12> which results from some rotation about the orientation < 1 12> afford a splendid wear-resistant property. Namely, the inventors have found out that the Ni-Fe - Nb series and Ni-Fe-Ta series alloys can be appreciably improved in wear-resistant property by forming recrystallization texture of 1"11 Ok 1 12> +1311 k 1 12>.

The inventors have made many researches based on this finding to form a recrystallization 55 texture of 111 01< 1 12>+1131 1 J< 1 12> of the Ni-Fe-Nb series and Ni-Fe- Ta series alloys.

Though it has been known that Ni-Fe series binary alloys form therein after cold rolling thereof a worked aggregated texture of 1111 01< 1 12> +11 12k 111 > and a heat treatment of the texture at a high temperature develops a recrystallization texture of i'1001<001>, the inventors have found out that a recrystallization texture of 11 101<1 12>+131 1i<1 12> can be effectively 60 formed with remarkably improved wear-resistant property by adding Nb and/or Ta into the Ni-Fe series binary alloys thereby decreasing stacking fault energy, cold working the added alloy at a working ratio of at least about 50%, and heating the cold working alloy at a high temperature of at least about 900'C.

By the addition of Nb and/or Ta into the Ni-Fe series alloy, specific electric resistance of the 65 2 GB2170222A 2 alloy is improved and crystal grains of the alloy become minute, so that eddy current toss in an AC magnetic field is decreased to increase the effective permeability of the alloy.

To sum up, by the effect of addition of Nb and/or Ta to the Fe-Ni series alloys, a recrystalliza- tion texture of 111 01< 1 12> +1311 1< 1 12> of the alloys is developed well and the effective permeability of the alloys is exceedingly increased, so that excellent wear-resistant-alloy of high 5 permeability can be obtained.

In order to produce the alloy according to the present invention, aw appropriate amount of a mixture or an alloy comprising about 60-90% by weight of Ni, about 0.5- 14% by weight of Nb and the remainder of Fe, is melted in an appropriate melting furnace in vacuo, in air or preferably in a non-oxidizing atmosphere such as hydrogen, argon, nitrogen or the like. Alternatively. the. 10 above melt is further added with at least one subsidiary component selected-from the group consisting of each not over than about 7% by weight of CrI Mo, Ge and Au, each not over than about 10% by weight of Co and V, not over than about 15% by weight of W, not over than about 20% by weight of Ta, each not over than about 25% by weight of Cu and -Mn, each not - over than about 5% by weight of At, Si, Ti, Zr, Hf, Sn, Sb, Ga, In, TI (thallium), Zn, Cd, rare 15 - earth elements and platinum group elements., each not over than about 3% by weight of Ag. Sr and Ba, each not over than about 1 % by weight-of B and P, and not over than about 0.1% of S. The sum of the subsidiary components is about 0.01-30% by weight of the total melt. If necessary, an appropriate amount-of C, Mg andlor Ca (each 0.3% by weight or less) is added to the melt to enhance forgeability and workability of cooled melt or ingot. Thus obtained melt 20 of mixture is thoroughly agitated to obtain a melt alloy of a uniform composition.

The melt alloy is -then poured into a mould of an appropriate shape and size to obtain a wholesome ingot. The-ingot is not rolled or forged. at a high temperature to a, suitable shape such as a rod or plate, and, if necessary, annealed. The ingot of suitable shape is then cold worked at a working ratio of at least about 50% by means of e.g. cold rolling to a desired 25 shapd such as a- thin plate. of a thickness of 0. 1 mm. From the thin plate an annular plate of an - outer diameter of 45 mm and an inner diameter of 33 mm is punched out. The.alloy of a shape of an annular plate is heated in vacuo, air or a non-oxidizing atmosphere such as hydrogen, argon, nitrogen orthe like at a temperature of at least about 90OoC and below the m.p. of the annular plate for an appropriate time, and then cooled from a temperature which is equal to or 30 higher than an order-disorder transformation point (about 60WC) of the alloy to a room tempera ture at an appropriate cooling rate of about 1 OWC/sec- 1'C/hr depending on composition of the plate. Alternatively, the cooled alloy is reheated to a temperature which is-equal to or lower than the transformation point of the alloy for an appropriate time of about 1 min-1 00 hrs- depending on the alloy composition, and then cooled to a room temperature. 35 In this way, an exceeedingly wear-resistant alloy of high permeability of a recrystallization texture of 11 1011<1 12>+131 ltt<l 12> and having an effective permeability of at least about 3,000 at 1 KHz and a saturation magnetic flux density of not less than about 4,000 G is obtained.

For a better understanding of the present invention, reference is made to the accompanying 40 drawings, in which:

Figure 1 is a characteristic graph of 79.5%Ni-Fe-Nb series alloys showing relations between the Nb amount and the characteristic properties of the alloys; Figure 2 is a characteristic graph of 79.5%Ni-Fe-7%Nb series alloy showing relations between - the cold working ratio and the characteristic properties iricluding-the recrystallization texture of- 45 the alloy; Figure 3 is a characteristic graph of 79.5%Ni-Fe-7%Nb series alloy showing relations between the heating temperature and the characteristic properties including the recrystallization texture of the alloy; Figure 4 is a characteristic graph of 79%Ni-Fe-3:5%Nb- series alloy (alloy No. 15), 79.5%Ni-Fe- 50 7%Nb series alloy (alloy No. 23). and 82.5%Ni-Fe-5%Nb series alloy (alloy No. 38) showing- - -- relations between the -cooling rate and the effective permeability with_ the parameters of reheat ing-time and temperaure of the alloys; Figure 5 is a characteristic graph of 79%Ni-Fe-Nb-Ta series alloys showing relations- between - the amount of Nb+Ta and the characteristic properties including the recrystallization textur of 55.

the alloys, Figure 6 is a characteristic graph of 79%Ni-Fe5%Nb-5%Ta series alloy showing relations between the cold working ratio and the characteristic properties including the recrystallization texture of the alloy; Figure 7 is a characteristic graph of 79%Ni-Fe-5%Nb-5%Ta series -alloy showing -a rela - tion - 60 between the heating temperature and the characteristic properties including the recrystallization texture of the alloy.

Figure 8 is a characteristic graph of 80,3%Ni-Fe-2%Nb-2%Ta-3%Ge series alloy.(alloy No.

263), 79.5%Ni-Fe-5%Nb-3%Ta-2%MO series alloy (alloy No. 257) and MNi-Fe5%Nb-5%Ta series alloy (alloy No. 227) showing relations between the cooling rate and the- effective permea- 65 3 GB2170222A 3 bility with parameters of reheating temperature and time of the alloys; Figure 9 is a characteristic graph of MNi-Fe-5%Nb-5%Ta series alloy added with Cr, Mo, Ge, Au or Co showing relations between the amount of each element and the characteristic properties of the alloy; Figure 10 is a characteristic graph of 79%Ni-Fe-5%Nb-5%Ta series alloy added with V, W, Cu 5 or Mn showing relations between the amount of each element and the characteristic properties of the alloy; Figure 11 is a characteristic graph of MNi-Fe-5%Nb-5%Ta series alloy added with AI, Si, Ti, Zr, Hf, Sn, Sb, Ga, In or TI showing relations between the amount of each element and the characteristic properties of the alloy; and 10 Figure 12 is a characteristic graph of 79%Ni-Fe-5%Nb-5%Ta series alloy added with Zn, Cd, La, Pt, Be, Ag Sr, Ba, P, S or B showing relations between the amount of each element and the characteristic properties of the alloy.

Referring in more detail to Fig. 1, the characteristic curves represent relations between the Nb amount and the characteristic properties such as effective permeability lie, abrasion amount of a 15 magnetic head A expressed in pm and stacking degree of the recrystallization texture in arbitrary scale of 79.5% (by weight) Ni-Fe- Nb series alloys obtained by cold rolling at a working ratio of 98%, heating at 1,150'C, and cooling at a rate of 1,000'C/hr.

Ni-Fe-Nb series alloys produce therein worked aggregated texture of 11101 < 1 12> + 11121< 111 - if worked by cold rolling. If the cold worked alloy is heated to a high temperature, 20 a recrystallization textures of 11001<O0l> and 11 101<1 12+131 11<'I 12> is formed. Now, if Nb is added to the Ni-Fe series alloys to form Ni-Fe-Nb series alloys, the recrystallization texture of 11001<O0l> is prevented from forming in the cold worked and heat treated alloys, while the recrystallization texture of 111 O< 1 12> +1311 1< 1 12> is developed in the alloys accompanied by the decrease of the abrasion of the alloy. Effective permeability of the alloy is increased by 25 the addition of Nb. If the amount of Nb is less than about 0.5% by weight, the effect of addition of Nb is small, ' while if the amount of Nb is over than 14% by weight, forgeability and workability of the alloy become worse, so that an Nb amount in a range of about 0.5-14% by weight is preferable.

Referring in more detail to Fig. 2, the characteristic curves represent relations between-the 30 cold working ratio in % and the effective permeability lie, the abrasion amount A of the magn tic head in lim or the stacking degree of the recrystallization texture in arbitrary scale of 79.5% by weight Ni-Fe-7% by weight Nb alloy obtained by heating at a temperature of 1,150'C and cooling. Increase of the cold working ratio of the alloy causes to develop the recrystalliza tion texture of-11 10<1 12>+131 l<1 12> in the alloy and raise or improve the effective 35 permeability of the alloy. This phenomenon is particularly noticeable when the cold working ratio is at least about 50%.

Referring in more detail to Fig. 3, the characteristic curves represent relations between the heating temperature and the effective permeability lie, the abrasion amount A of the magnetic head in pm or the stacking degree of recrystallization texture in arbitrary scale of 79.5% by 40 weight Ni-Fe-7% by weight Nb alloy obtained by cold rolling ratio of 98% and heating. With the increase of the heating temperature the 11 121< 111 > component is decreased and the Ill 1 Ok 1, 12> +1311 k 1 12> component is developed to improve the wear- resistant property of the alloy as well as the effective permeability. This phenomenon is particularly noticeable at a heating temperature of about 900'C or more. 45 Referring in more detail to Fig. 4, the characteristic curves show relations between the cooling rate and. the effective permeability lie of 79% by weight Ni-Fe3.5% by weight Nb alloy (alloy No. 15) 79.5% by weight Ni-Fe-7% by weight Nb alloy (alloy No. 23) and 82. 5% by weight Ni Fe-5% y weight Nb-3% by weight Cr alloy (alloy No. 38) obtained by cold working, heating and cooling. In the drawing effective permeability values with symbol -xrepresent values of those 50 alloys obtained by reheating and cooling.. It can be understood from the drawing that an optimum cooling rate, an optimum reheating temperature and an optimum reheating time exist depending on composition of the alloys. Referring in more detail to Fig. 5, the characteristic curves show relations between a sum of equal weight amounts of Nb and Ta and the effective permeability lie, the abrasion amount, A of 55 a magnetic head in pm and the -stacking degree of the recrystallization texture in arbitrary scale of 79% by weight- Ni-Fe-Nb-Ta series alloys (wherein weight ratio of Nb:Ta=1:1) obtained by cold rolling of a working ratio of 90%, heating at 1,100'C and cooling at a cooling rate of BOOT/hr. Though- Ni-Fe-Nb-Ta series alloys produce therein worked aggregated texture of 111 O[< 1 12> +11 12< 111 > when worked by cold rolling and produce therein the recrystalliza- 60 tion textures of 1100<001> and 111 101<'I 12>+131 l[<l 12> when worked at a high tempera ture, the recrystallization texture of 11001<0Oll> is prevented from forming and the recrystalliza tion texture of 11 101<l 12>+131 11<'I 12> is developed accompanied by the decrease of the abrasion amount, if Nb and Ta are added to produce the alloy. The effective permeability of the -65 alloy is increased by the addition of Nb and Ta. If the sum of Nb and Ta is less than about 65 4 GB2170222A 4 0.5% by weight, the effect of addition of Nb+Ta is small, while if the sum of Nb+Ta is over than about 200/a by weight, the forgeability and the workability of the alloy become worse, so that the sum of Nb+Ta in a r - ange of about 0.5-20% by weight is- preferable..

Referring in more detail to Fig. 6, the characteristic curves show relations between the cold working ratio in % and the effective permeability lie, the abrasion amount A of a magnetic head 5 in lim and the stacking degree of the recrystallizatiOn texture in arbitrary scale of 79% by weight Ni-Fe-5% by weight Nb-5% by weight Ta alloys obtained by Cold working and heating at 1, 1 00'C. Increase of the cold working ratio brings development of the recrystallization structure of {l 101<1 12>-+131 11<1 12>, improves the wear-resistant property of the alloy and promote the effective permeability. This phenomenon is particularly noticeable at a working ratio of at 10 least about 50%.

Referring in more detail to Fig 7, the characteristic curves show relations between the heating temperature and the effective permeability lie, the abrasion amount A of a magnetic head in urn and the stacking degree of the -recrystallization texture in arbitrary scale of 79% by weight Ni-Fe- 5% by weight Nb-5% by weight Ta alloys obtained by cold rolling of a cold working ratio of - 15 85% and heating at various temperatures. With the increase of the heating temperature, the 11 121<'I 1 l> component is decreased while the texture of 11 101<1 12>+131 11<'I 12> is devel-oped to increase the wear-resistant property as we[[-as the effective permeability. This phenomenon is particularly noticeable at a temperature of about 900'C or more.

Referring in more detail to Fig. 8, the characteristic curves show relations between the _20 -effective permeability and the. cooling rate of 80.3% by weight Ni-Fe-2% by weight Nb-2% by weight Ta-3% by weight Ge alloy (alloy No. 263), 79.5% by weight Ni-Fe-5% by weight Nb-M by weight Ta-2% by weight Mo alloy (alloy No. 257) and 79% by weight Ni- Fe-5% by weight Nb-5% by weight Ta alloy (alloy No. 227) oilatained by cold working and heating at respective temperature and time. In the drawing, the symbol "x" represents values of the effective permea- 25 bility of the alloys which Were subjected to respective reheating temperature and time as shown in the drawing. It can be seen that there are existent an optimum cooling rate, an optimum reheating temperaure and an optimum reheating time.

- Referring in more detail to Fig. 9, the characteristic curves show relations between the addition amount of a subsidiary component Cr, Mo, Ge, Au or Co and the abrasion amount A of a 30 magnetic head in lim or the effective permeability lie of 79% by weight Ni-Fe-5% by weight Nb 5% by weight Ta alloy added with the subsidiary component. By- the addition of the subsidiary component, the effective permeability of all alloys are'increased and the abrasion amount is decreased. However, if the amount of Cr, Mo, Ge or Au is more than about 7% by weight, the saturation magnetic flux- density becomes less than about 4,000 G, so that the addition of the - -- 35 component of more than about 7% by weight is- not preferable. Also, - addition of Co of more than about 10% is not preferable, because magnetic remanence is increased to increase noise due to magnetization of the magnetic head, Referring in more detail to Fig. 10, the characteristic curves show relations between the amount of a subsidiary component V, W, Cu or Mn and the effective permeability lie or the - 40 abrasion amount A of a magnetic head in lim of 79% by weight NiFe-5% by weight Nb-5% by weight Ta alloy added with the subsidiary component. By the addition of V, W, Cu_orMn, the effective permeability of alloys is increased, while the abrasion amount of the alloys is decreased. However, addition of V of more than about 1Mby weight, addition of W of more than about 15% by weight and addition of Cu or Mn of more than about 25% by weight is not 45 preferable, because the saturation magnetic flux density becomes less than about 4,000 G.

Referring in more detail to Fig. 11, the characteristic curves show relations between the amount of a subsidiry component M. Si, Ti, Zr, Hf, Sn-.. Sb, Ga, In or TI and the effective permeability lie or the abr asion amount A of a magnetic head in urn. By the- addition of AI, -Si, 50 - - - Ti, Zr, Hf, Sn, -Sb, Ga, In or TI, the effective permeability of the alloys is increased,- while the abrasion amount is decreased. However., if Si, Ti, Zr, Hf, Ga, In, or Tl is added more- than about 5% by weight, the saturation magnetic flux density becomes less than - about -4,000 G, so that it is not preferable. Addition of AI. Sn or Sb of more than about 5% by weight is not preferable, because the alloy becomes difficult to-be forged.

- Referring in more detail to Fig. 12, the: characteristic curves show relations between the amount of a subsidiary component Zn, Cd, La, Pt, Be, Ag, Sr, Ba, P, S or B and -the effective - permeability lie or the abrasion amount A of a magnetic head in pm of 79% by Weight Ni-Fe-5% by weight Nb-5% by weight Ta alloy added with the subsidiary component.-- By the addition of the subsidiary component the effective permeability of the alloys is increased, while the abrasion amount of the alloy is decreased. However, addition of--Zn, Cd, La or Pt of more than about 5% 60 by weight or addition of Be, Sr or Ba of more than about 3% by weight is not preferable, - because the saturation magnetic flux density becomes less than about 4, 000 G, and addition of Ag of more than about 3% by weight, P or B of more than about 1% by weight or S of more than about 0.1% by weight is not preferable, because the alloy becomes difficult to be worked by forging. 65- GB2170222A 5 In the present invention, cold working of the alloy is necessary or essential to form cold worked aggregated texture of 111 01< 1 12> +11 121< 111 > and to develop the recrystallization texture of 111 01< 1 12> +1311 J< 1 12> based on the texture of 111 01< 1 12> + 11 12< 111 >. As seen from Figs. 1, 2, 5 and 6, in case when Nb or the sum of Nb and Ta is more than about 0.5% by weight, particularly after the alloy is cold worked at a cold working ratio of at least 5 about 50%, development of the recrystallization texture of 11 101<1 12>+ 131 l<1 12> is remar kable, the wear-resistant property. of the alloy is improved appreciably as well as the effective permeability of the alloy.

In the present invention also, the heating effected subsequent to the cold working is necessary in homogenizing the alloy texture, removing strain caused by the cold working, and developing 10 the recrystallization texture of 11 101<1 12>+131 11<1 12> so as to obtain a high effective permeability and a splendid-wear-resistant property. Particularly, as seen from Figs. 3 and 7, by heating the cold worked alloy to a temperature of at least about 900'C and preferably below the m.p. of the alloy, the effective permeability and the wear-resistant property of the alloy are noticeably improved. 15 If the aforementioned cold working and the subsequent heating to a temperature of at least about 900'C and below the m.p. of the alloy are repeated, the stacking degree or the recrystalli zation texture of 11 101<] 12>+131 11<] 1,2> is enhanced effectively as well as-the wear resistant. property of the alloy. By the repetition of heating and cooling, even if a working ratio of final. cold workin is less than about 50%, the recrystallization texture of 20 11 101<J: 12>+13 1?<1 12> can be obtained, so that such case of repetition falls. within the scope of the technical concept of the present invention. Therefore, the cold working ratio of the present invention means a total of one or two cold workings throughout the whole production steps, and does not mean solely the cold working ratio in the final cooling step.

Though the cooling of the alloy from a temperature of about 900'C or more and below the 25 m.p. of the alloy to a temperature of about an order-disorder transformation point (about 60OoC) of the alloy does not have a great influence on the magnetic property of the alloy regardless whether the cooling is quenching or annealing, the cooling rate below the transformation point have a great influence on the magnetic property of the alloy as seen in Figs. 4 and 8. This is, by cooling the alloy from a temperature below the transformation point to a room temperature 30 at an appropriate rate in a range of about 100'C/sec-l'C/hr depending on the composition of the alloy, a degree of ordering in the matrix of the alloy is suitably adjusted to afford an excellent magnetic property of the alloy. If the alloy is cooled rapidly at a cooling rate slightly higher than about 100'C/sec within the above cooling rate range, the degree of ordering in the alloy becomes small. If the alloy is cooled down more rapidly than the above cooling rate, 35 degree of ordering is not promoted and the regularity of crystals becomes to a further small value to deteriorate the magnetic property of the alloy. However, if the alloy of such small degree of ordering is reheated at a temperature of about 200-600'12 which is equal to or below the transformation point. of the alloy for a time of about 1 min-100 hrs depending on the composition of the alloy, then the degree of ordering in the alloy is promoted to a suitable 40 regularity to improve the magnetic property of the alloy. On the other hand, if the alloy is annealed at a slow cooling rate e.g. of smaller than about M/hr from a temperature which is equal to or above the transformation point, then the degree of ordering in the alloy is promoted too much so that the magnetic property of the alloy becomes inferior.

The above heating and/or reheating is preferably effected in an atmosphere containing hydro- 45 gen, because it is particularly effective in increasing the effective permeability of the alloy.

A reason of limiting the composition of the alloy of the present invention to about 60-90% by weight of Ni, about 0.5-14% by weight of Nb or about 0.5-20% by weight of Nb+Ta (with the understanding that Nb:-5-about 14% by weight) and the remainder of Fe, and limiting the subsidi ary component to about 0.01-30% by weight of at least one component selected from the 50.

group consisting of each about 7% by weight or less of Cr, Mo, Ge and Au, each 10% by weight or less of Co and V, about 15% by weight or less of W, about 20% by weight or less of Ta, each about 25% by weight or less of Cu and Mn, each about 5% by weight or less of AI, Si, Ti, Zr, Hf, Sn, Sla, Ga, In, TI, Zn, Cd, rare earth elements and platinum group elements, each about 3% by weight or less of Be, Ag, Sr and Ba, each about 1% by weight or less of B 55 and P, and about 0. 1 % by weight or less of S, is that the alloy outside this composition range has an inferior magnetic property of wear-resistant property, though the alloy within this compo sition range has an effective permeability of at least about 3,000 at 1 KHz, a saturation magnetic flux density of at least about 4,000 G, the recrystallization texture of 111 01< 1 12> +1311 < 1 12> and an excellent wear-resistant property, as shown in the 60 Examples, the attached drawings, and the Tables 4 and 5 which will later be described.

If Nb or the sum of Nb+Ta is less than about 0.5% by weight, the recrystallization texture of 11 O< 1 12> + 1311 < 1 12> does not develop sufficiently, so that the alloy is inferior in wear resistant property. While, if Nb is more than about 14% by weight or the sum of Nb+Ta is more than about 20% by weight, the alloy becomes difficult to forge and the saturation 65 6 GB2170222A 6 magnetic flux density becomes less than about 4,000 G.

The alloy of the present invention having a composition of about 60-90% by weight of Ni.

about 0.5-14% by weight of Nb or about 0.5-20% by weight of the sum of Nb+Ta (with the understanding the Nb is about 14% by weight or less), and the remainder of Fe, has, a high effective permeability at least about 3,000 at 1 KHz, a good saturation magnetic flux density of 5 at least about 4j000 G, a splendid wear-resistant property, and an excellent workability. If the alloy is further added with at least one subsidiary component of Cr, Mo, Ge, Au, W. Ta, V, Cu, Mn, AI, Zr, Si, Ti, Ht Ga, In TI, Zn, Cd, rare earth element, platinum group element, Be, Ag, Sr, Ba, B, P and S etc., the effective permeability of the alloy is generally remarkably increased. If the alloy is added with Co, the saturation magnetic flux density of the alloy is enhanced. If the 10 alloy is added with at least one of Au, Mn, Ti, Co, rare earth element, platinum group-element, Be, Sr, Ba and B, the forgeability and the workability of the alloy -is improved. If -the alloy is added with at least one of AI, Sn ' Sb, Au, Ag, Ti, Zn, Cd, Be, P, S and V, the recrystallization - texture of 11001<1 12>+131 11<1 12:- is developed properly to improve the wear-resistant 15- property of-the alloy. 15 The alloy-of the pre - sent invention is easy to forge and hot working. In addition, it has the recrystallization texture of 1110t<112>+13111<112>, so that it has a splended wear-resistant property, a superior satUr ation magnetic flux density of at least about 4,000 G, and a high - effective permeability of at least about 3,000 at 1 KHz. Therefore, the alloy is suitable well as a magnetic head for magnetic record play-back- apparatuses as well as a magnetic material for 20 general electro-magnetic apparatuses and devices-which require wearresistant property and high permeability.

Hereinafter, the present invention will -be explained in more detail with reference to Examples - which however should not be construed by any means as limitations of the present invention. Irt the following Examples, all % of alloy components are shown by weight basis, unless otherwise --25 specified.

Example 1

Preparation of an alloy of a composition of Ni=79.5%, Nb=7%. and Fe=the remainder (alloy No. 23). -30 As raw materials, electrolytic nickel having a purity of 99.8%, electrolytic iron having a purity - of 99.9% and niobium metal of a purity of 99.8% are used. For preparing a sample, the raw materials in a total weight of 800 9 is put into an alumina crucible, melted in vacuo in a high frequency induction electric furnace, agitated well to yield a homogeneous melt of alloy. The melt is poured into a mould having a cavity of a diameter of 25 mm and a height of 170 mm. 35 The resultant ingot is forged at a temperature of about 1,100'C to obtain a plate of a thickness of 7 mm. The plate is hot rolled at a temperature of about 900-1,2000C to obtain an appropri ate thickness, and subsequently cold rolled with various working ratio at an ambient temperature to a thin plate of 0.1 mm thickness. Then, annular plates of an outer diameter of 45 mm, and an_ inner diameter of 33 mm are punched out from the thin plate. 40 Thereafter, the annular plates are treated with various heat treatments to produce cores of a mag etic head. Magnetic property of the heat treated plate is measured, while abrasion at a humidity of 80% and a temperature of 4WC by running a CrO, magnetic. tape for 20,0 hrs - thereover are also measur ed by means of Talisurf surface roughness meter. The results are shown in Table 1. 45 7 GB2170222A 7 Table 1

Effective Saturation Coercive Abrasion Cold working and perme- magnetic force amount 5 heat treatment abiliijetY fluLd(eGn)s 'ty Hc(Oe) A(pm) Cold rolled at a working 10 ratio of 25%, heated in hydrogen at 1,1500C for 10,000 6,750 0.0320 135 2 hrs, and cooled at a rate of 1,0000C/hr 15 Cold rolled at a working ratio of 70%, heated in hydrogen at 1,150C for 16,700 6,780 0.0195 42 2 hrs, and cooled at 20 a rate of 1,o000C/hr Cold rolled at a working ratio of 98%, heated in hydrogen at 700C for 1,500 6,730 0.3300 130 25 3 hrs, and cooled at a rate of 1,o000C/hr Cold rolled at a working 30 ratio of 98%, heated in 13,100 6,770 0.0210 45 hydrogen at 1,0000C for 2 hrs, and cooled at a rate of 1,0000C/hr Cold rolled at a working ratio of 98%, heated in hydrogen at 1,1500C for 18,000 6,800 0.0180 31 2 hrs, and cooled at 40 a rate of 1,0000C/hr Cold rolled at a working ratio of 98%, heated in hydrogen at 1,250'C for 17,500 6,790 0.0190 25 45 1 hr, and cooled at a rate of 1,0000C/hr Cold rolled at a working ratio of 99%, heated in 18,300 6,800 0.0170 31 50 hydrogen at 1,1SO'C for 1 hr, and cooled at a rate of 1,0000C/hr 8 GB2170222A 8 Example 2

Preparation of an alloy of a composition of Ni=79%, Nb=5%, Ta=5% and Fe=the remainder (alloy No. 227).

As raw materials, nickel, iron and niobium having the same purities as those of Example 1 and tantalum of a purity of 99.8% are used. From the raw materials, samples annular plates are 5 prepared in the similar manner as in Example 1. The sample annular plates cold worked by various cold working ratio are treated with various heat treatment to produce cores of a magnetic head. Magnetic property of the heat treated plate is measured, while abrasion amounts of the cores at a humidity of 80% and 4WC by running a CrO, magnetic tape for 200 hrs thereover are also measured. The results are shown in Table 2. 10 9 GB2170222A 9 Table 2

Effective Saturation Coercive Abrasion Cold working and perme- magnetic heat treatment ability flux dens force amount 5 pe Bs(G) 'ty Hc(Oe) A(pm) Cold rolled at a working ratio of 30%, heated in 10 hydrogen at 1,1SO'C for 28,000 6,030 0.0124 110 2 hrs, and cooled at a rate of 201C/hr Cold rolled at a working 15 ratio of 70%, heated in hydrogen at 1,150C for 30,900 61,040 0.0081 25 2 hrs, and cooled at a rate of 201C/hr 20 Cold rolled at a working ratio of 98%, heated in hydrogen at HO'C for 24,500 6,030 0.0142 105 3 hrs, and cooled at 25 a rate of 200C/hr Cold rolled at a working ratio of 98%, heated in 30 hydrogen at 1,000'C for 32,600 6,040 0.0050 is 3 hrs, and cooled at a rate of 200C/hr Cold rolled at a working 35 ratio of 98%, heated in hydrogen,at 1,150'C for 38M0 6,050 0.0032 13 2 hrs, and cooled at a rate of WC/hr 40 Cold rolled at a working ratio of 98%, heated in hydrogen at 1,2501C for 37,500 6,050 0.0044 12 1 hr, and cooled at 45 a rate of 20C/hr Cold rolled at a working ratio of 98%, heated in 50 hydrogen at 1,3501C for 36,200 6,040 0.0063 10 2 hrs, and cooled at a rate of 20C/hr 1 t 1 t t GB2170222A 10 Example 3

Preparation of an alloy of a composition of Ni=80.1%, Nb=7%, P=0.2%, S=0. 05%, Mo=2% and Fe=the remainder (alloy No. 182).

As raw materials, nickel, iron and niobiurn having the same purities as those of Example 1, molybdenum of a purity of 99.8%, ferrophosphoalloy of a phosphorus content of 25%, and iron 5 sulfide of a sulfur content of 25%, are used. From the raw materials, sampie annular plates are prepared in the similar manner as in Example 1. The sample annular plates cold worked by various cold working ratio are treated with various heat treatment to produce cores of a magnetic head. Magnetic property of the heat treated plate is measured, while abrasion amounts of the cores at a humidity of 80% and 40'C by running a CrO, magnetic tape for 200 hrs 10 thereover are also measured. The results are shown in the following Table 3.

Characteristic properties of typical alloys are shown in the following Tables 4 and 5.

GB2170222A 11 Table 3

Cold working and Effective Saturation Coercive Abrasion perme- magnetic force amount 5 heat treatment ability flux density Hc(Oe) A(pm) Me Bs(G) Cold rolled at a working ratio of 30%, heated in 10 hydrogen at 1,100C for 21200 5,900 0.0152 115 2 hrs, and cooled at a rate of SOOC/hr Cold rolled at a working 15 ratio of 70%, heated in hydrogen at 1,1000C for 23,700 5,910 0.0124 23 2 hrs, and cooled at a rate of 501C/hr 20 Cold rolled at a working ratio of 95%, heated in hydrogen at 8001C for 13,600 5,890 0.0530 125 3 hrs, and cooled at 25 a rate of 50C/hr Cold rolled at a working ratio of 95%, heated in 30 hydrogen at 1,000'C for 25,100 5,910 0.0100 17 3 hrs. and cooled at a rate of SOOC/hr Cold rolled at a working 35 ratio of 95%, heated in hydrogen at 1,100'C for 26,800 5,930 0.0095 is 2 hrs, and cooled at a rate of 500C/hr 40 Cold rolled at a working ratio of 95%, heated in hydrogen at 1,2501C for 26,500 5,930 j 0.0098 12 1 hr, and cooled at 45 a rate of 500C/hr Cold rolled at a working ratio of 95%, heated in 50 hydrogen at 1,3501C for 25,200 5,920 0.0110 11 2 hrs, and cooled at a rate of SOIC/hr i Table 4(a)

Alloy Composition Cold Heating Cooling Reheating Effective Saturation Coercive Abrasion (the remainder is Fe) working temper- perme- magnetic No. Subsidiary ratio ature rate Temper- Time ability flux force amount (OC/hr) ature density (0e) A (pm) Ni Nb component (OC) (OC) (hr) pe (liKHz) (G) 7 78.3 1.5 --- 95 1,200 40p000 - - 101100 9,700 0.0341 70 79.0 3.5 --- 90 1,100 80P000 350 10 15,000 8,400 0.0210 so 23 79.5 7.0 --- 98 1,150 1,000 - - 18,000 6,800 0.0180 31 80.7 11.5 --- 80 1,050 4,000 400 2 15,800 4,500 0.0204 24 38 82.5 5.0 Cr 3.0 90 1,100 200 420 5 29,500 5,820 0.0081 18 46 79.0 3.0 Mo 2.0, Sr 0.2 95 1,050 100 - 22,000 7,100 0.0113 19 78.0 8.5 Ta 0.3, La 0.7 98 1,200 50 - 24,600 6,000 0.0095 17 63 79.5 10.0 Ba 0.2, Co 3.0 95 1,150 400 400 1 25,300 5,350 0.0090 is 71 80.0 4.0 Ge 1.5, Ga 0.5 90 1,150 800 - - 23,700 6,840 0.0105 18 79 76.3 5.5 W 3.0, P 0.1 98 1,200 200 - - 27,200 7,200 0.0086 18 87 81.5 3.0 V 1.5, B 0.1 95 1,000 800 - - 23,100 7,530 0.0110 16 69.0 4.0 CU 11.0, Ba 0.2 90 1,250 1,000 350 8 26,300 6,710 0.0090 19 G) CC) NJ -j (D N NJ N NJ i0' Table 4(b)

Alloy Composition Cold Heating Cooling Reheating Effective Saturation Coercive Abrasion (the remainder is Fe) working temper- perme- magnetic No. Subsidiary ratio ature rate Temper- Time ability flux force amount (OC/hr) ature density (0e) A (pm) Ni Nb component (%) (OC) (hr) pe (lKHz) (G) (OC) 103 79.5 7.5 Al 0.5, Zn 0.5 98 1,050 20 - - 24,800 6,240 0.0098 is 112 78.2 5.0 Si 1.0, Sb 1.0 85 1,100 400 - - 23,000 6,680 0.0117 16 79.0 6.5 Ti 1.0, In 1.0 95 1,050 800 380 5 27,900 5,860 0.0090 is 128 80.5 7.0 Zr 1.0, Tl 1.0 90 1,100 200 - - 28,200 5,930 0.0084 17 79.7 5.3 Hf 1.5, Sn 0.5 98 1,100 400 - - 24,700 6,300 0.0096 is 143 79.5 6.5 Be 0.5) Mn 5.0 98 1,050 800 - - 23,600 6,410 0.0114 13 152 80.3 6.0 Cd 0-3, mo 1.0 90 1,150 1,000 400 3 26,400 6,590 0.0098 1-5 79.6 5.0 Au 2.0, Ce 1.0 95 1,200 200 - - 22,800 6,140 0.0120 18 169 79.8 2.5 Ta 0.49 Pt 1.0, 95 1,300 50 - - 21,700 6,700 0.0157 17 Mo 3.0 75.3 6.5 S 0.03, W 5.0 98 1,150 400 380 4 24,600 6,060 0.0107 is 182 80.1 7.0 P 0.2, S 0.05, 95 1,100 50 - 26,800 5,930 0.0095 15 Mo 2.0 G) W 0 P.

Table 5(a)

1 G) W 0 N.) Alloy Composition Cold Heating Cooling Reheating Effective Saturation Coercive Abrasion (the remainder is Fe) working temper- rate Temper- perme- magnetic force amount flux No. Subsidiary ratio ature (OC/hr) Time abili density (0e) A (pm) ature ty Ni Nb Ta (OC) (OC) (hr) pe MHz) (G) component 69.5 0.2 17.5 --- 95 1,150 1,000 350 5 18,600 6,050 0.0184 17 208 73.8 1.2 14.0 --- 98 1,100 400 - - 20,500 6,640 0.0150 18 215 74.5 3.0 10.0 --- 95 1,050 200 - - 21,800 7,860 0.0122 17 227 79.0 5.0 5.0 --- 90 1,100 200 - - 23,000 7,310 0.0110 20 235 79.5 8.0 2.0 --1,050 100 - - 22,700 6,080 0.0115 21 242 79.3 10.0 0.3 --- 90 1,200 1,000 400 1 20,700 5,020 0.0147 17 250 75.7 2.0 12.0 Cr 2 90 1,200 1,000 380 5 32,500 6,360 0.0057 11 257 79.5 5.0 3.'0 Mo 2 98 1,150 20 - - 38,400 6,050 0.0032 13 263 80.3 2.0 2.0 Ge 3 95 1,100 20,000 350 20 27,700 6,210 0.0107 12 270 80.0 4.0 5.5 Au 2, Al 0.5 90 1,000 100 - - 26,900 6,150 0.0100 10 276 68.0 10.5 7.0 Co 5, Sa 0.5 95 l150 800 420 1 27,200 7,730 0.0140 13 284 80.3 5.0 1.5 V 3, Tl 1 90 1,050 50 - - 31,000 6,840 0.0076 12 292 67.5 3.0 12.0 CU 10, Hf 1 95 1,000 10,000 350 5 28,300 6,360 0.0085 10 301 80.2 7.0 5.0 Mn 3, Cd 1 85 1,200 400 - - 27,600 6,520 0.0103 10 310 78.7 3.0 10.0 Si 1.5, In 1 98 1,150 200 - - 29200 5,970 0.0075 9 318 80.3 8.5 0.4 Ti 1, Pt 0.5 90 1,050 100 - - 27,500 5,930 0.0094 12 G' Table 5 (b)

Composition Cold 1 Reheating Effective Saturation Heating Alloy (the remainder is Fe) working temper- Cooling perme- magnetic Coercive Abrasion flux force No. ratio ature rate Temper- Time ability amount Ni Nb Ta Subsidiary (OC) (OC/hr) ature (lKHz) density (0e) A (pm) (hr) component ( OC) Me (G) 325 68.5 1.0 14.0 W 5, La 0.5 80 1,250 400 380 2 31,700 5,580 0.0066 11 332 79.8 5.5 3.0 Zr 1, Cr 1 90 1,100 100 - - 28,400 5,960 0.0084 13 341 79.5 2.5 8.0 Zn 1.5, mo 1 95 1,150 so - - 30,600 6,720 0.0075 13 353 78.0 1.8 12.0 Sb 0.7, V 1.5 95 1,050 200 - - 29,000 6,370 0.0080 11 360 77.0 7.0 7.0 Ga 1, Cu 3 90 950 800 - - 289400 5,900 0.0091 13 365 72.0 0.7 15.0 Be 0.5, W 3 95 1,100 1,000 400 2 31,600 6,120 0.0072 11 373 79.5 7.0 2.0 Ru 1.5 90 1,200 100 - - 29,500 6,580 0.0086 12 381 76.3 2.0 13.0 Ag 0.7, Mn 1 90 1,050 1,000 350 10 27,300 7,240 0.0110 10 393 79.0 6.0 2.5 Sr 1, mo 1 85 1,100 so - - 31800 6,500 0.0073 12 399 77.5 3.0 10.0 Ba 1, si 1 95 1,050 1,000 - - 29,000 6y270 0.0(;-r- 13 407 78.5 6.0 7.0 B 0.3, Ti 1 90 1,100 800 - - 28Y600 6,180 0.01,n,7 13 415 77.2 4.0 5.0 P 0.3, W 4 95 1,150 1,000 400 1 27,400 6,480 0.0103 10 423 79.5 5.5 4.5 S 0.02, Mo 3 98 1,200 200 - - 26200 6,130 0,0') 12 Perm- 78.5 --- 98 1Y100 10,000 - 2800 10,800 110 alloy -1 16 GB2170222A 16 As clearly apparent from the foregoing detailed explanation, the alloy of the present invention has a splendid wear-resistant property, a good saturation magnetic flux density of at least about 4,000 G, a high effective permeability of at least about 3,000 at 1 KHz and a low coercive force, so that it is suited well for not only a magnetic alloy for a easing or core of a magnetic head of a magnetic record play-back apparatus, but also for a magnetic material for general 5 electromagnetic apparatuses and devices which necessitate a splendid wear- resistant property and an excellent high permeability. In addition, the alloy of the present invention is easy to forge or hot working. Thus, the present invention is eminently useful industrially.

Although the present invention has been explained with reference to specific values and embodiments, it will of course be apparent to those skilled in the art that the present invention 10 is not limited thereto and many variations and modifications are possible without departing from the broad aspect and scope of the present invention as defined in the appended claims.

Claims

1. A wear-resistant alloy of high permeability, comprising by weight about 60-90% of Ni, 15 about 0.5-14% of Nb, and the remainder of Fe with unavoidable impurities, and having an effective permeability of at least about 3,000 at 1 KHz, a saturation magnetic flux density of at least about 4,000 G, and a recrystallization texture of 11 101<1 12>+131 'I'f<1 12>.

2. A wear-resistant alloy of high permeability, comprising by weight about 60-90% of Ni and about 0.5-14% of Nb as main components; about 0.01-30% of at least one subsidiary compo- 20 nent selected from the group consisting of each not over than about 7% of Cr, Mo, Ge and Au, each not over than about 10% of Co and V, not over than about 15% of W, not over than about 20% of Ta, each not over than about 25% of Cu and Mn, each not over than about 5% of A], Si, Ti, Zr, Hf, Sn, Sb, Ga, In, TI, Zn, Cd, rare earth elements and platinum group elements, each not over than about 3% of Be, Ag, Sr and Ba, each not over than about 1 % of 25 B and P, and not over than about 0. 1 % of S; and the remainder of Fe as a main component with a minor amount of unavoidable impurities, and having an effective permeability of at least about 3,000 at 1 KHz, a saturation magnetic flux density of at least about 4,000 G, and a recrystallization texture of '11 10!<1 12>+131 11<1 12>.

3. A method of producing a wear-resistant alloy of high permeability, comprising, cold work 30 ing an alloy comprising by weight about 60-90% of Ni, about 0.5-14% of Nb and the remain der of Fe with a minor amount of unavoidable impurities at a cold working ratio of at least about 50%, heating the cold worked alloy at a temperature which is at least about 90WC and below the m.p. of the alloy, and subsequently cooling the heated alloy to a room temperature from a temperature higher than an order-disorder transformation point of the alloy at a cooling rate of 35 about 1OWC/sec-VC/hr depending on the alloy composition, whereby the alloy is provided with an effective permeability of at least about 3,000 at 1 KHz, a saturation magnetic flux density of at least about 4,000 G, and a recrystallization structure of ll M<1 12>+ IS1 l<1 12>.

4. A method of producing a wear-resistant alloy of high permeability, comprising, cold work- ing an alloy comprising about 60-90% by weight of Ni, about 0.5-14% by weight of Nb and 40 the remainder of Fe with a minor amount of unavoidable impurities at a cold working ratio of at least about 50%, heating the cold worked alloy at a temperature which is at least about 90WC and below the m.p. of the alloy, subsequently cooling the heated alloy from a temperature which is higher than an order-disorder transformation point of the alloy at an appropriate cooling rate of about 1OWC/sec-1'C/hr depending on the alloy composition, reheating the cooled alloy to a 45 temperature which is below the order-disorder transformation point of the alloy for an appropriate time of about 1 min- 100 hrs depending on the alloy composition, and cooling the reheated alloy, whereby the alloy is provided with an effective permeability of at least about 3,000 at 1 KHz, a saturation magnetic flux density of at least about 4,000 G, and a recrystallization texture of 11 10k1 12>+31 1k1 12>. 50

5. A method of producing a wear-resistant alloy of high permeability, comprising, cold work- ing an alloy comprising by weight about 60-90% of Ni and about 0.5-14% of Nb as main components; about 0.01-30% of at least one subsidiary component selected from the group consisting of each not over than about 7% of Cr, Mo, Ge and Au, each not over than about 10% of Co and V, not over than about 15% of W, not over than about 20% of Ta, each not 55 over than about 25% of Cu and Mn, each not over than about 5% of AL Si, Ti, Zr, Hf, Sn, Sb, Ga, In, TI, Zn, Cd, rare earth elements and platinum group elements, each not over than about 3% of Be, Ag, Sr and Ba, each not over than about 1% of B and P, and not over than about 0. 1 % of S, and the remainder of Fe as a main component with a minor amount of unavoidable impurities at a cold working ratio of at least about 50%, heating the cold worked alloy at a 60 temperature which is not less than about 90WC, and below the m.p. of the alloy, subsequently cooling the heated alloy to a room temperature from a temperature higher than an order-disorder transformation point of the alloy at an appropriate cooling rate of about 100'C/sec-VC/hr depending on the alloy composition, heating the cold worked alloy at a temperature which is not less than about 90WC and below the m.p. of the alloy, and subsequently cooling the heated 65 17 GB2170222A 17 alloy, from a temperature which is higher than the order-disorder transformation point of the alloy to a room temperature at an appropriate cooling rate of about 100'C/sec-l'C/hr depending on the alloy - composition, whereby the alloy is provided with an effective permeability of at least about 3,000, a saturation magnetic flux density of at least about 4,000 G, and a recrystallization texture of 111 01< 1 12> +1311 1< 1 12>. 5

6. A method of producing a wear-resistant alloy of high permeability, comprising, cold woking an alloy comprising by weight about 60-90% of Ni and about 0.5-14% of Nb as main components; about 0.01-30% of at least one subsidiary component selected from the group consisting of each not over than about 7% of Cr, Mo, Ge and Au, each not over than about 10. 10% of Co and V, not over than about 15% of W, not over than about 20% of Ta, each not. 10 over than about 25% of Cu and Mn, each not over than about 5% of AI, Si, Ti, Zr, Hf, Sn, Sb, Ga, In, TI, Zn, Cd, rare earth elements and platinum group elements, each not over than about 3% of Be, Ag, Sr and Ba, each not over than about 1% of B and P, and not over than about 0. 1 % of S; and the remainder of Fe as a main component with a minor amount of unavoidable impurities at a working ratio of at least about 50%, then heating the cold worked alloy at a 15 temperature which is not less than about 900T and below the m.p. of the alloy, subsequently cooling the heated alloy from a temperature which is higher than an order- disorder transforma tion point of the alloy at an appropriate cooling rate of about 100'C/sec- I'C/hr depending on the alloy composition, then reheating the cooled alloy at a temperature of not over than the order-disorder transformation point of the alloy for an appropriate time of about 1 min-100 hrs 20 depending on the alloy composition, and cooling the reheated alloy, whereby the alloy is provided with an effective permeability of at least about 3,000 at 1 KHz, a saturation magnetic flux density of at least about 4,000 G, and a recrystallization texture of - 111 01.<'I 12> +1311 1< 1 12>.

7. A wear-resistant alloy of high permeability, comprising by weight about 60-90% of Ni, 25 about 0.520% of a sum of Nb+Ta (with the understanding that Nb is not over than about 14%), and the remainder of Fe with a minor amount of unavoidable impurities, and having an - effective permeability of at least about 3,000 at 1 KHz, a saturation magnetic flux density of at least about 4,000 G, and a recrystallization texture of ill 10[<l 12>+131 11<l 12>.

8. A wear-resistant alloy of high permeability, comprising by weight about 6090% of Ni and 30 about 0.5-20% of a sum of Nb+Ta (with the understanding that Nb is not over than about 14%) as main components; about 0.01-30% of at least one subsidiary component selected from the group consisting of each not over than about 7% of Cr, Mo, Ge and Au, each not over than about 10% of Cp and V, not over than -15% of W, each not over than about 25% of Cu and Mn, each not over than 5% of AI, Si, Ti, Zr, Hf, Sn, Sb, Ga, In, TI, Zn, Cd, rare earth 3.5 elements and platinum group elements, each not over than 3% of Be, Ag, Sr and Ba, each not over than about 1 % of B and P, and not over than about 0. 1 % of S; and the remainder of Fe as a main component with a minor amount of unavoidable impurities, and having an effective permeability of at least about 3,000 at 1 KHz, a saturation magnetic flux density of at least about 4,000 G, and a recrystallization texture of 11 10[<l 12>+131 11<l 12>. -40

9. A method of producing a wear-resistant alloy of high permeability, comprising, cold work- ing an alloy comprising by weight about 60-90% of Ni, about 0.5-20% of a sum of Nb+Ta (with the understanding that Nb is not over than about 14%) and the remainder of Fe with a minor amount of unavoidable impurities at a working ratio of at least about 50%, heating the cold worked alloy at a temperature below the m.p. of the alloy and not less than about 900T, 45 and subsequently cooling the heated alloy to a room temperature from a temperature which is higher than an order disorder transformation point of the alloy at an appropriate cooling rate of about 100T/sec-1T/hr depending on the alloy composition, whereby the alloy is provided with an effective permeability of at least about 3,000 at 1 KHz, a saturation magnetic flux density of at least about 4,000 G, and a recrystallization texture of 11 101<l 12>+ 131 l<1 12>. 50

10. A method of producing a wear-resistant alloy of high permeability, comprising, cold working an alloy comprising by weight about 60-90% of Ni, about 0.5-20% of a sum of - Nb+Ta (with the understanding that Nb is not over than about 14%) and the remainder of Fe with a minor amount of unavoidable impurities of a cold working ratio of at least about 50%, heating the cold worked alloy at a temperature which is below the m.p. of the alloy and not less 55 than about 900T, cooling the heated alloy from a temperature which is higher than an orderdisorder transformation point of the alloy at an appropriate cooling rate of about 100T/sec1'C/hr- depending on the alloy composition, reheating the cooled alloy at a temperature of not over than the order-disorder transformation point of the alloy for an appropriate time of about 1 min-100 hrs depending on the alloy composition, and cooling the reheated alloy, whereby the 60 alloy is provided with an effective permeability of at least about 3,000 at 1 KHz, a saturation magnetic flux density of at least about 4,000 G, and a recrystallization texture of 11101<112>+13111<112>. -

11. A method of producing a wear-resistant alloy of high permeability, comprising, cold working and alloy comprising by weight about 60-90% of Ni and about 0.5- 20% of a sum of 65 18 G132170222A 18 Nb+Ta (with the understanding that Nb is not over than 14%) as main components;- about.

0.01-30% of at least one subsidiary component selected from the group consisting of each not over than about 7% of Cr, Mo, Ge and Au, each not over than about -1.0% of Co and V, not over than about 15% of W, each not over than about 25% of Cu and Mn, each not over than about 5% of AI, Si, Ti, Zr, Hf, Sn, Sb, Ga, In, TI, Zn, Cd, rare earth elements and platinum 5 group elements, each not over than about 3% of Be, Ag, Sr and Ba and each not over than about 1 % of B and P; and the remainder of Fe as a main component with a minor amou-nt of unavoidable impurities at a cold working ratio of at least about 50%, heating the cold worked alloy at a temperature which. is below the m.p. of the alloy and not less than about 900T,- and.

1G subsequently cooling the, heated alloy from a temperature which is higher than an order-disorder 10 transformation point of the, alloy to a room temperature at an appropriate cooling rate of about 100'Clsec-l'C/hr depending on the alloy composition, whereby the alloy is provided with an effective permeability of at least about 3,000 at 1 KHz, a saturation magnetic flux density of at least about 4,000 G, and a recrystallization texture of 111 01< 1 12> + 1311 [< 1 12>.

12. A method of producing a wear-resistant alloy of high permeability, comprising, cold 15 working an alloy comprising -by weight about 60-90% of Ni and about 0.5- 20% of a sum of Nb+Ta (with the understanding that Nb is not over than about 14%) as main components; - about 0.01-30% of it least one subsidiary component selected from the group consisting of each not over than about 7% of Cr, Mo, Ge and Au, each not over than about 10% of Co and V, not over than about 15% of W, each not over than about 25% of Cu and Mn, each- not over 20 than, about 5% of A], Si, Ti, Zr, Hf, Sn, Sb,-Ga, In, TI,_Zn, Cd, rate earth elements and platinum group elements, each not over than about 3% of Be, Ag, Sr and Ba, each not over than about - - 1 % of B and P, and not over than about 0. 1 % of S; and the remainder of Fe with a minor amount of unavoidable impurities at a cold working ratio of at least- about 50%, heating the cold 2-5 worked alloy at a temperature which is below the m.p. of the alloy and not less than about 25 90WC, subsequently cooling the heated alloy from an order-disorder transformation point of the alloy at an appropriate cooling rate of 100T/sec-VC/hr depending on the alloy composition, reheating the cooled alloy at a temperature which is not over than the order-disorder transforma - tion point of the alloy for an appropriate time of about 1 min-1.00 hrs depending on the alloy composition, and cooling the reheated alloy, whereby the alloy is provided with. an effective 30 permeability of at least about 3,000 at 1 KHz, a saturation magnetic flux. density of at least about 4,000 G, and a recrystallization texture of 11 101<1 12>+131 11<1 12>.

13. A wear-resistant alloy of high permeability, comprising by weight about 60-900/0- of Ni, ab out 0.5-14% of Nb and about 0.001-5% of Zn as main components; about 0. 01-30% of at least one. subsidiary component selected from the group consisting of each not over than about 35 7% of Cr, Mo, Ge -and Au, each not over than- about 10% of Co and V, not over than about -. - 15% of W, not-over than about 20% of Ta, each not over than about 25% of Cu and Mn, each not over than about 5% of AI, Si, Ti,Zr, Hf, Sn, Sb, Ga, In, TI, Cd, rare earth elements and platinum group elements, each not-over than about 3% of Be, Ag, Sr and Ba, each not-over than about 1% of B and P, and not over than about 0.1% of S; and the remainder of Fe- as a 40 main component with a -minor amount of unavoidable impurities, and having an effectIve permea bility of at least about 3,000 at 1 KHz, a saturation magnetic flux density of at least about 4,000 G, and a recrystallization texture of 1 101kl 12>+131 l[<l 12>.

14. A wear-resistant alloy of high permeability, comprising by- weight about 60-90% of Ni, about 0.5-14% of Nb and about 0.001-5% of Cd as main- components; about 0.01-30% of at 45 leas one subsidiary corrfponent selected from the group consisting of each not over- than about - 7% -of -Cr, Mo, Ge and Au, each not over than about 10% of Co and V, not over than about 15% of W, not over than about 20% of Ta, each not over than about 25% of Cu and Mn, each not over than about 5% of AI Si, Ti, Zr, Hf, Sn, Sb, Ga, In, TI, Zn, rare earth elements and platinum group elements, eaJ not over than about 3% of Be, Ag,- Sr and Ba, each not over 50-- than about 1% of B and P, and not over than about 0.1% of S,- and the remainder of Fe as a main component with a minor amount of unavoidable impurities, and having an effective permea-bility of at least about 3,000 at 1 KHz, a saturation magnetic flux density of at least about 4,000 G, and a recrystallization texture of h 10[<l 12>+131 1 [<l 12>.

15. A wear-resistant alloy of high permeability, comprising, by weight about 6090% of Ni, 55 about 0.5-14% of Nb and about 0.001-5% of TI-as main components; about 0. 01-30% of at least one subsidiary component selected from the group consisting of each not over than about 7% of Cr, Mo, Ge and Au, each not- over than about 10% of Co and V, not over than about 15% of W, not over than about 20% of Ta, each not over than about 25% of Cu and Mn, each - not over than about 5% of AI, Si, Ti, Zr, Hf, Sn, Sb, Ga, In, Zn, Cd, rare earth elements and 60 platinum group elements, each notover than about 3% of Be, Ag, Sr and_Ba, each not over than ab t 1 OX of B and P, and not over than about 0. 1 % of S; and the remainder of Fe as a - 1 main co%uponent with a minor amount of unavoidable impurities, and having an effective permea bilitY of at least about 3,000 at 1 KHz, a saturation magnetic flux density of at least about 4,000 G, and a recrystallization texture of h 1 01< 1 12> +1311 < 1 12>. @5 19 GB2170222A 19

16. A wear-resistant alloy of high permeability, comprising by weight about 60-90% of Ni, about 0.5-14% of Nb and about 0.001-7% of Mo as main components; about 0. 01-30% of at least one subsidiary component selected from the group consisting of each not over than about 7% of Cr, Ge, and Au, each not over than about 10% of Co and V, not over than about 15% of W, not over than about 20% of Ta, each not over than about 25% of Cu and Mn, each not 5 over than about 5% of A], Si, Ti, Zr, Hf, Sn, Sb, Ga, In, TI, Zn, Cd, rare earth elements and platinum group elements, each not over than about 3% of Be, Ag, Sr and Ba, each not over than about 1 % of B and P, and not over than about 0. 1 % of S; and the remainder of Fe as a main component with a minor amount of unavoidable impurities, and having an effective permea- bility of at least about 3,000 at 1 KHz, a saturation magnetic flux density of at least about 10 4,000 G, and a recrystallization texture of 111 01< 1 12> +1311 1< 1 12>.

17. A wear-resistant alloy of high permeability, comprising by weight about 60-90% of Ni, about 0.5-14% of Nb and about 0.001-5% of rare earth element as main components; about 0.01-30% of at least one subsidiary component selected from the group consisting of each not over than about 7% of Cr, Mo, Ge and Au, each not over than about 10% of Co and V, not 15 over than about 15% of W, not over than about 20% of Ta, each not over than about 25% of Cu and Mn, each not over than about 5% of AI, Si, Ti, Zr, Hf, Sn, Sla, Ga, In, TI, Zn, Cd and platinum group elements, each not over than about 3% of Be, Ag, Sr and Ba, each not over than about 1 % of B and P, and not over than about 0. 1 % of S; and the remainder of Fe as a main component with a minor amount of unavoidable impurities, and having an effective permea- 20 bility of at least about 3,000 at 1 KHz, a saturation magnetic flux density of at least about 4,000 G, and a recrystallization texture of 11 101<1 12>+131 11<1 12>.

18. A wear-resistant alloy of high permeability, comprising by weight about 60-90% of Ni, about 0.5-14% of Nb and about 0.001-5% of Hf as main components; about 0.01-30% of at least one subsidiary component selected from the group consisting of each not over than about 25 7% of Cr, Mo, Ge and Au, each not over than about 10% of Co and V, not over than about 15% of W, not over than about 20% of Ta, each not over than about 25% of Cu and Mn, each not over than about 5% of AI, Si, Ti, Zr, Sn, Sb, Ga, In, TI, Zn, Cd, rare earth elements and platinum group elements, each not over than about 3% of Be, Ag, Sr and Ba, each not over than about 1 % of B and P, and not over than about 0. 1 % of S; and the remainder of Fe as a 30 main component with a minor amount of unavoidable impurities, and having an effective permea bility of at least about 3,000 at 1 KHz, a saturation magnetic flux density of at least about 4,000 G, and a recrystallization texture of 111 01< 1 12> +1311 1< 1 12>.

19. A wear-resistant alloy of high permeability, comprising by weight about 60-90% of Ni, about 0.5-14% of Nb and about 0.001-1% of B as main components; about 0. 01-30% of at 35 least one subsidiary component selected from the group consisting of each not over than about 7% of Cr, Mo, Ge and Au, each not over than about 10% of Co and V, not over than about 15% of W, not over than about 20% of Ta, each not over than about 25% of Cu and Mn, each not over than about 5% of AI, Si, Ti, Zr, Hf, Sn, Sla, Ga, In, TI, Zn, Cd, rare earth elements and platinum group elements, each not over than about 3% of Be, Ag, Sr and Ba, not over than 40 about 1% of P, and not over than about 0.1% of S; and the remainder of Fe as a main component with a minor amount of unavoidable impurities, and having an effective permeability of at least about 3,000 at 1 KHz, a saturation magnetic flux density of at least about 4,000 G, and a recrystallization texture of 11 10< 1 12> +1311 1< 1 12>.

20. A wear-resistant alloy of high permeability, comprising by weight about 60-90% of Ni, 45 about 0.5-14% of Nb and about 0.001-1% of P as main components; about 0. 01-30% of at least one subsidiary component selected from the group consisting of each not over than about 7% of Cr, Mo, Ge and Au, each not over than about 10% of Co and V, not over than about 15% of W, not over than about 20% of Ta, each not over than about 25% of Cu and Mn, each not over than about 5% of AI, Si, Ti, Zr, Hf, Sn, Sb, Ga, In, TI, Zn, Cd, rare earth elements and 50 platinum group elements, each not over than about 3% of Be, Ag, Sr and Ba, each not over than about 1 % of B, and not over than about 0. 1 % of S; and the remainder of Fe as a main component with a minor amount of unavoidable impurities, and having an effective permeability of at least about 3,000 at 1 KHz, a saturation magnetic flux density of at least about 4,000 G, and a recrystallization texture of 1h 1 01< 1 12> +131 1;k 1 12>. 55

21. A wear-resistant alloy of high permeability, comprising by weight about 60-90% of Ni, about 0.15-14% of Nb and about 0.001-0.1% of S as main components; about 0.01-30% of at least one subsidiary component selected from the group consisting of each not over than about 7% of Cr, Mo, Ge and Au, each not over than about 10% of Co and V, not over than about 15% of W, not over than about 20% of Ta, each not over than about 25% of Cu and Mn, each 60 not over than about 5% of AI, Si, Ti, Zr, Hf, Sn, Sb, Ga, In, TI, Zn, Cd, rare earth elements and platinum group elements, each not over than about 3% of Be, Ag, Sr and Ba, and each not over than about 1 % of B and P; and the remainder of Fe as a main component with a minor amount of unavoidable umpurities, and having an effective permeability of at least about 3,000 at 1 KHz, a saturation magnetic flux density of at least about 4,000 G, and a recrystallization texture of 65 GB2170222A 20, 11 101<1 12>+131 11<1 12>.

22. A wear-resistant alloy of high permeability, comprising by weight about 60-90% of Ni, about 0.5-14% of Nb and about 0.001-1% of a sum of P+ S (with the understanding that S is not over than 0.1%) as main components; about 0.01-30% of at least one subsidiary compo- nent selected from the group consisting of each not over than about 7% of Cr, Mo, Ge and Au, 5 each not over than about 10% of Co and V, not over than about 15% of W, not over than about 20% of Ta, each not over thans about 25% of Cu and Mn, each not over thariv about 5% of AI, Si, Ti, Zr, W, Sn, Sb, Ga, In, TI, Zn, Cd, rare earth elements and -platinum group elements, each not over than about 3% of Be, Ag, Sr and Ba, and not over than about 1 % of B; and the remainder of Fe as a main component with a minor amount of unavoidable impurities, 10 and having an effective permeability of at least about 3,000 at 1 KHz, a saturation magnetic flux density of at least about 4,000 G, and a recrystallization texture of 111 01< 1 12>+131 1 J< 1 12>.

Printed in the United Kingdom for Her Majesty's Stationery Office. Del 8818935. 1986, 4235. Published at The Patent Office, 25 Southampton Buildings, London, WC2A 1 AY, from which copies may be obtained.